Structural and UV-blocking properties of carboxymethyl cellulose sodium/CuO nanocomposite films

Nanoparticles have made a substantial contribution to the field of skincare products with UV filters in preserving human skin from sun damage. The current study aims to create new polymer nanocomposite filters for the efficient block of UV light that results from the stratospheric ozone layer loss. The casting approach was used to add various mass fractions of copper oxide nanoparticles (CuO-NPs) to a solution of carboxymethyl cellulose (CMC). The amorphous nature of CMC was revealed by XRD analysis, with the intensity of the typical peak of virgin polymer in the nanocomposite spectrum decreasing dramatically as the doping amount was increased. The FTIR spectra revealed the functional groups of CMC and the good interaction between the CMC chain and CuO-NPs. Optical experiments revealed that the optical transmittance of pure CMC was over 80%, whereas it dropped to 1% when CuO-NPs content was increased to 8 wt.%. Surprisingly, the inclusion of CuO-NPs considerably improved the UV blocking property of the films extended from the UV region (both UV-A: 320–400 nm and UV-B: 280–320 nm) to the visible region. Optical band gap of CMC decreased sharply with increasing CuO concentration. The tunable optical characteristics can be utilized in UV- blocking filters and various optoelectronics applications.

Sunlight has a variety of positive effects in humans, including the production of vitamin D and the reduction of β-endorphin expression, both of which improve well-being 1 . The loss of the stratospheric ozone layer has resulted in a gradual increase in UV radiation in recent decades. This increases the number of negative health effects on humans, such as skin burns, photoaging, immune system damage, and skin cancer 1,2 . As a result, the number of skincare products with UV filters has risen rapidly, helping to protect human skin from sun damage. There were 26.9 million tonnes of products used worldwide that had UV filters, with modern consumption presumably being substantially greater 3 . UV filters are often used in a variety of personal care items, including lotions, shampoos, creams, aftershaves, and cosmetics [4][5][6] .
Photo protective techniques predate the introduction of the first sunscreen in the 1900s, and ancient civilizations have long employed plant extracts to protect their skin from sunburns 7 . Many of the photo protective chemical components found in natural extracts are now used in sunscreens 7 . In fact, the majority of UV filters are derived from natural sources, such as plant, animal, or mineral compounds 7 . The photo protective effect of benzyl salicylate against UV-B radiation was discovered in 1928, but it was first commercialized in 1935 in the first sunscreen, "Ambre Solaire" 8,9 .
Based on their capacity to absorb UV radiation (UVR), UV filters are classified as UV-A, UV-B, or broadspectrum UV filters (UV-A and UV-B) 10 . UV-A wavelengths ranged from 320 to 400 nm. Additionally, these groups can be divided into organic and inorganic filters, with organic filters having the ability to just absorb UVR and inorganic filters having the ability to reflect and scatter UVR 11 .
The safety of UV filters for both people and the environment has come under scrutiny recently. Further investigation into the effectiveness of UV filters used topically on the skin has revealed a progressive decline in their UV-protective ability that cannot just be attributable to photo-induced degradation. Researchers that looked into the causes of this behavior came to the conclusion that UV filters might be routinely absorbed via the skin's surface or even discharged during bathing and washing activities 12,13 . Numerous studies were conducted in an the structure and purity of the samples. The XRD pattern of CuO-NPs was collected in the range of 2θ = 25°-85° as presented in Fig. 1a, with peaks at 2θ = 32.51°, 35 where, n is the order of X-rays diffraction, λ is the wave's incidence wavelength, d is the plane separation between lattices, and θ is the scattering angle. The diffraction peak's broadening can be utilized to estimate the crystallite size of powder samples. In addition, the crystallite size was estimated utilizing the Debye-Scherrer equation 39 : where, D is the crystalline size in nanometers, k is the Scherrer's constant (0.9), λ is the X-Ray wavelength, θ is peak position, and β is the full width at half-maximum (FWHM) of the diffraction peak. The average crystallite size of the prepared CuO-NPs was calculated and equals 34.01 nm.
The following equations were used to calculate micro strain (ε), dislocation density (δ), and the number of crystallites (N c ) based on the obtained data (see Table 2).
The XRD patterns of a virgin CMC and CMC with different quantities of CuO-NPs are shown in Fig. 1b. It can be seen that the CMC matrix and loading CuO-NPs films have a broad peak near 2θ = 20° due to the amorphous nature of the CMC. It could also be deduced that the intensity of this peak decreases with the addition of CuO-NPs. The changes could be attributed to the interaction between the CMC and the CuO-NPs. Furthermore, more inter-and intramolecular attraction could occur, softening the polymer backbone. It is well known that peak  Fig. 1b) occurs as a result of two major effects: crystallite size reduction and microstrain generation in the material's crystal structure. As a result, by analyzing peak broadening, it is possible to gain insight into the material's associated properties. Similar results were reported for CMC films 40 . The addition of CuO-NPs as nanofiller to a pristine CMC matrix was confirmed by the presence of a number of remarkable peaks of CuO-NPs, an increase in peak intensity with increasing CuO content, and a decrease in CMC diffraction peak intensity (see Fig. 1b). Furthermore, substantial reflections can be seen in the XRD measurements along the (-111), (111) and (-113) planes of all nanocomposites. This reflection planes corresponds to the sharp diffraction peaks around 35.53°, 38.79°, and 61.62°. Moreover, as the CuO-NPs concentration in the polymer matrix increased to 8 wt.%, the XRD intensity along these reflections increased. Additionally,  www.nature.com/scientificreports/ micro strain, dislocation density, and number of crystallites were calculated for the most prominent peak in the nanocomposite films (see Table 2). The values of dislocation density and micro strain increased with increasing CuO-NPs concentration, as shown in the table. Also, the sample abbreviated as B4 (contains 8wt.% CuO) possesses a dislocation density and micro strain higher than that of CuO-NPs. Furthermore, as demonstrated by XRD intensity fluctuations in doped films, variations in vacancy and defect density cause significant changes in grain boundaries and thus lattice strain. The number of crystallites in the nanocomposite films increased as the CuO-NPs content increased. The number of crystallites ranged from 0.02 to 11.43. As the CuO-NPs concentration increased, the broadening of the diffraction peak (-111) narrowed, as shown in Fig. 1b, as the number of crystallites (Nc) increased. These results confirm the influence of CuO-NPs on the crystallinity of pure CMC. The reason for increasing the number of crystallites with CuO-NPs addition is the decrease in crystallite size, where the number of crystallites is inversely proportional to the crystallite size as presented in Eq. (5). This reflects the good dispersion of CuO-NPs in the nanocomposite.
Fourier transform infrared spectroscopy (FTIR) analysis. Understanding the chemical and structural properties of the synthesized CMC, as well as the impact of CuO-NPs, is critical and is satisfied utilizing FTIR analysis. The CuO-NPs can be identified by the tree distinctive bands found at 447 cm −1 , 478 cm -1 , and 579 cm −1 (see Fig. 2a). The high-frequency mode at 579 cm −1 and the peak at 478 cm −1 can be attributed to the Cu-O stretching vibration. Additionally, no other IR active mode was seen between 600 and 660 cm −1 , ruling out the possibility of another phase, such as Cu 2 O 41 .
The FTIR spectra of a pure CMC and a CMC containing various concentrations of CuO-NPs (2, 4, 6 and 8 wt.%) are shown in Fig. 2b. The key feature bands of the virgin CMC are revealed in the FTIR spectrum. The broad band at 3261 cm −1 may be assigned to the O-H stretching vibration. The band at 2919 cm −1 may be due to the C-H asymmetrical stretching vibrations of the CH 2 . Carboxyl group (COO) asymmetric stretching and CH 2 scissoring vibration are responsible for the observed bands at 1585 and 1412 cm −1 , respectively. The presence of OH bending motion is demonstrated by the band at 1322 cm −1 .
Furthermore, the band at 1014 cm −1 was attributed to the C-O stretching, whereas the band at 906 cm −1 was caused by CH 2 rocking. The creation of intermolecular hydrogen bonding between the CMC and CuO-NPs of the nanocomposite films was expected, according to Saadiah et al. 42 , and so these actually occur at the bending OH region and asymmetric COO functional group of CMC. The integration of CuO-NPs influences the functional groups of CMC as a result of the interactions between these groups and CuO-NPs, as presented in Fig. 2b. With the addition of CuO-NPs, the strength of the OH stretching vibration band of the pure film at 3261 cm −1 reduced and shifted to a higher wave number, as seen in Fig. 2b. Additionally, the figure shows that all samples possess high intensity bands assigned to CuO-NPs from 400 to 600 cm −1 which may be due to the structural changes of CMC with CuO addition and the increased concentration of CuO-NPs. All of this evidence supports the formation of a hydrogen bond between CuO-NPs and pristine CMC, as well as providing important structural modification information.
With increasing CuO-NPs content, the intensity of C-H stretching, COO stretching, and CH-O-CH 2 stretching increased and shifted toward a higher wave number (see Table 3). Additionally, the intensity of CMC's absorption band assigned to the C-O-C bending vibration (1053 cm −1 ) was also increased, and this confirms that strong interaction occurred between CMC and CuO via this band. This reflects the good interaction between CMC chains and CuO-NPs supports the results of XRD analysis. Moreover, the strong absorption bands at 419 cm −1 revealed the stretching mode of Cu-O bond vibration in the monoclinic phase of CuO-NPs. All of this evidence supports the formation of a hydrogen connection between CuO-NPs and virgin CMC, as well as providing structural information 42 .
HRTEM analysis. Figure 3 shows the TEM micrographs of CuO-NPs synthesized by the precipitation method. The deposition of nanoparticle dispersions on the electron-transparent TEM gold grid results in a combination of CuO aggregates and their agglomerates, making it difficult to determine the true CuO-NPs aggregate size (which is obtained by XRD in the present study). The TEM investigation, on the other hand, clearly shows that the agglomerated aggregates are made up of clusters of considerably smaller original crystallites. The average crystallite size of nanoparticles is 40.34 nm as determined by TEM (see Fig. 3a), which is larger than the average crystallite size (34.01 nm) determined by XRD 43 . It is worth noticing that CuO-NPs have a single crystalline pattern with a monoclinic CuO phase, as demonstrated in Fig. 3b UV-blocking capacity. A UV-Vis spectrophotometer was used to measure the transmittance of the produced films at wavelengths ranging from 200 to 1000 nm (Fig. 4a). The results revealed that the CMC film containing 8 wt.% of CuO had a high UV-blocking capability, reaching 99% UV-B and UV-A blocking.
Again, we believe that the addition of CuO-NPs to the CMC solution had a significant impact on its ability to absorb UV-light in this investigation, since the addition of CuO-NPs to the CMC solution improved UV-blocking performance, particularly in the UV-A area. Figure 4a shows how 8 wt.% CuO-NPs additions can block 100% of UV-A (320-400 nm) and UV-B (280-320 nm). In comparison to 8 wt.% CuO-NPs, the addition of 2, 4, and 6 wt.% CuO-NPs resulted in a decrease in transparency, even though the UV-C (from 200 to 280 nm) and UV-B regions were not completely blocked at the CuO-NP concentrations used. As a result, CMC/ CuO with a concentration of 8 wt.% CuO-NPs was discovered to be the optimal percentage for successfully blocking UV radiation. These findings were in line with a prior study that found that adding lignin to cellulose-based films increases UV protection while decreasing transparency 21  www.nature.com/scientificreports/ 2% lignin that blocked 100% of UV-B and more than 90% of UV-A 21 .Similarly, when lignin was added to the PVA film at a higher concentration (3 wt%), effective UV-B blocking was found, but UV-A transmittance was not 43,44 . At 600 nm, Fig. 4b demonstrates the relationship of opacity for undoped CMC and nanocomposite films. Equation (6) was used to compute the opacity of the films 45 : where, A 600 is the absorbance at 600 nm and X is the film thickness (mm). A higher opacity number indicates that a film is less transparent. For all samples, the optical transmittance rose as the wavelength was raised. A www.nature.com/scientificreports/ simple visual examination of the prepared films reveals that their colour gradually changes from transparent to relatively dark grey and finally to black, with the CMC film being more transparent (lower opacity value) than films incorporating CuO-NPs (Fig. 4c). The percentage of light transmittance at wavelengths of 300 and 600 nm, on the other hand, is reported in Table 4. It was discovered that, when CMC is combined with CuO-NPs, the outcome is a decrease in the T% at λ = 300 and 600 nm, as it drops to around 1.10089% and 2.06329%, respectively. The transmittance of the composite is affected by a variety of factors, including intrinsic material properties such as particle size and refractive index of the components, as well as composite fabrication factors such as nanocomposite thickness, filler concentration, surface roughness, and particle dispersion state. Thus, particles with sizes larger than the visible wavelength would obstruct light, leading to translucent or opaque films. Due to the absence of light-blocking particles, the pure CMC film has the highest percent transmittance (Fig. 4a). Another possible explanation for the decreased transparency of the nanocomposite films is that the agglomerations of CuO-NPs became a barrier to the penetration light. When nanofillers are added to a transparent polymer matrix, transparency is lost, resulting in an opaque nanocomposite. Actually, the matrix can be thought as a non-absorbing, uniform medium through which light flows without deflection. Light interferes with the particles when different refractive index fillers are added. Blocking or filtering of UV is caused by two processes: UV light absorption and UV light scattering. The Rayleigh theory describes how particle size and the difference in refractive index between particles and medium affect light scattering 40 .
The outcomes revealed that the addition of CuO-NPs resulted in a significant decrease in light transmission in both UV and visible light regions. It's worth noting that CuO-NPs' inclusion had a stronger effect in the UV region than in the visible region, meaning that the film's UV barrier characteristics were improved while its transparency was lowered. Because UV rays have high oxidizing properties and can have a negative impact on human health and food packaging, blocking UV rays is critical in the food human care and packaging industry 46 .  www.nature.com/scientificreports/ Optical band gap determination using the absorption spectra fitting model. In this work, the absorption spectrum model (ASF) was applied to calculate optical energy band deviations for the nanocomposites studied, utilizing the UV absorption spectra measured 47 . The ability to calculate the optical gap energy ( E ASF Opt ) of the samples without having to assess their thickness distinguished this method. The calculation is solely based on the samples' absorbance data. According to Souri and Shomalian, the optical gap energy depends on the wavelength of the incident photon and is expressed as follows:  Table 5. These values are fairly close to those found using Tauc's model 46 . The E ASF Opt for indirect transitions of the samples altered with the alteration of CuO-NPs concentration, according to the results, the  The fundamental absorption edge and optical gap. The band gap value of amorphous materials such as polymers must be determined before they can be used. The most common method for inducing the band gap of amorphous materials is to employ optical absorption coefficient measurements to determine the fundamental absorption edge associated with the gap. For accurate determination of the absorption edge, the absorption coefficient was determined using the measured transmittance (T) and reflectance (R) values according to the following equation:  www.nature.com/scientificreports/ where d is the thickness of the film. Figure 5b depicts the variation in the absorption coefficient with incident light for pure and doped CMC films. As can be seen, the pure CMC film absorbs significantly in the UV spectral region, showing a high degree of amorphousness. Plotting the coefficient of absorption for all produced films versus the photon energy (hv) revealed the position of the absorption edge, as seen in Fig. 5b. The extrapolation of the linear part of the curve, for all samples, to the energy axis gives the value of the fundamental edge. A continuous red shift may be seen in the graph by increasing the CuO-NPs concentrations in the CMC matrix. Changes in the electron-hole in the conduction and valence bands are used to explain the absorption edge shift in the UV region. The decrease in the optical bandgap for nanocomposite films anticipates this result. Controlling material use in optical and electrical technologies entails identifying the optical energy gap, as previously discussed. Indeed, Mott and Davis 48 claim that the optical gap E g for non-crystalline materials may be calculated using the following formula: where α is the absorption coefficient, h is the plank's constant, ν is the incident frequency, B is a constant, E g is the optical band gap, and r is a constant that depends on the transition type; r = 1/2 for allowed direct transition and 3/2 for forbidden direct transition, and r = 2 and 3 for indirect allowed and forbidden transitions, respectively.
All of these parameters reduce significantly when CuO-NPs concentration increased. This reduction occurs when CuO-NPs with a low energy band gap are added to the high bandgap energy CMC matrix. E g is calculated by projecting the straight portion of the (αhν) 1/2 versus (hν) plot to the energy axis at αhν = 0 and assuming indirect transitions between the valence band and the conduction band in CuO (Fig. 6a). CuO-NPs have an estimated Eg value of 1.55 eV, which is comparable with CuO-NPs values reported in the literature 49,50 . In addition, Chand et al. 51 found E g values for CuO-NPs ranging from 2.90 to 3.60 eV, depending on the pH of the solution. In the inset of Fig. 6a, the absorption spectra of CuO-NPs are displayed as a function of λ, and a (9) (αhν) = B hν − E g r Figure 6. (a) variation of (αhν) 2 of CuO-NPs versus photon energy together with the absorption spectra of CuO-NPs in the inset of the figure (b) plot of ln (αhυ) versus ln (hυ-E g ) for pure CMC and (c: g) presents the plot of (αhν) 1 www.nature.com/scientificreports/ band of absorption appears around 396 nm. The position of the absorption band in these findings is dependent on the particle size of the CuO-NPs that have been produced 50,52 . The transition type and the optical band gap value of CMC can be determined by dividing Tauc's equation by the product of the differentiation, as described by the following equation 53 : Figure 6b shows the dependence of ln (αhυ) on ln (hυ-E g ) for Pure CMC. The value of r can be determined by plotting ln(αhυ) against ln(hυ-E g ). For pure CMC, from the slope of Fig. 6b, r is nearly equal to 2 in Eq. (10). This implies that the fundamental shoulder of absorption for pure CMC is formed by the indirect allowed transitions. Figure 6c presents the plot of (αhν) 1/2 as a function of photon energy (hν) for pure CMC, while Fig. 6d-g, present the plot of (αhν) 1/2 versus hν for CMC doped with 2, 4, 6, and 8 wt.% CuO-NPs, respectively. The gap energy is calculated for pure CMC and the nanocomposite films and listed in Table 5. From the table, pure CMC has only one indirect band gap, which is equal to 5.27 eV as shown in Fig. 6c, which is in good agreement with the reported data 53 . The addition of different weight percentages of CuO-NPs (2, 4, 6, and 8 wt.%) to CMC reduces the HOMO/LUMO bandgap of CMC from 5.27 to 3.14 eV during the filling process of the CMC with CuO-NPs.
The displacement of the adsorption edge and the decrease in gap energy with increasing filler content confirms the presence of an interaction between the Nano-filler and the polymer's functional groups. The addition of different weight percentages of CuO-NPs (2, 4, 6 and 8 wt. %) to CMC reduces the indirect bandgap of CMC (5.27 eV) until reach to 1.13 eV (for the sample denoted B4), as seen in the inset of Fig. 6g. On this concern, the addition of CuO-NPs creates localized states inside the bandgap, the transition between such states results in a bandgap value less than the HOMO/LUMO bandgap. The formation of localized states inside the bandgap as a result of doping has been previously mentioned in Euvrard et al. (2018) and El-Naggar et al. (2022) 54,55 . www.nature.com/scientificreports/ Due to the creation of localized states within the valence band of CMC, it was discovered that all of the manufactured samples have two indirect band gaps. The highest values correspond to the HOMO/LUMO gap, and the second to the onset gap.
Furthermore, as previously indicated in the FTIR section, this decrease can be explained in terms of the creation of hydrogen bonds between CuO-NPs and the pure CMC. The decrease in E g of CMC films with increasing CuO-NPs concentration could also be explained by the formation of localized states in the band gap of the host polymer matrix, which operate as trapping and recombination centers. The comparatively wide bandgap of the pure CMC was decreased to match new optical and optoelectronic applications by this method of CuO-NPs filling. Because of the momentum conservation law, indirect band gap semiconductor materials are good candidates for UV-blocking applications. In indirect semiconductors, holes and electrons have different moments. Thus, to recombinantly fulfill the momentum conservation law, they need to do something with this uncompensated momentum. Electron and hole-pair momentum can be zero in direct band gap semiconductors, allowing them to simply recombinate. CuO-NPs filling as an environmentally benign material allows for the innovative purpose of customizing the optical bandgap of CMC.
Urbach energy determination. The rise of non-crystalline ordering in the CMC film by CuO-NPs and the emergence of localized states in the prohibited band are supported by the absorption edge's reduction. This may be proven by using the following formula to calculate the Urbach energy (E u ), which specifies the width of localized states within the forbidden gap 56 : where α o is a fixed number. Figure 7a  www.nature.com/scientificreports/ CuO-NPs concentration. Figure 7a shows the linear connections for all as-fabricated films between ln(α) and photon energy (hυ). The Urbach energy increases with CuO-NPs concentration, as shown in Fig. 7b. The E U of each sample was determined by fitting the plots linearly, and the results are shown in Table 6. The band tail widens from 0.21 eV (CMC) to 2.25 eV (sample B4). This finding supports the notion that when the CuO-NPs percentage in the CMC matrix increased, the degree of disorder rose and localized states in the forbidden band emerged, facilitating electron transitions 57 .

Evaluation of the refractive index and extinction coefficient. In optical communication and opti-
cal device design, the refractive index (n) is critical. The most common method for estimating the refractive index (n) is to employ reflectance (R) spectra, which have the following relationship with n 7 : Figure 8a depicts the relationship between n and wavelength (λ). The values of n dramatically decrease with increasing CuO-NPs content in most of the investigated range (200-750 nm), then increase with increasing CuO-NPs content in the nanocomposite films (as presented in the inset of Fig. 8a), where the intermolecular hydrogen bonding between CuO-NPs and the neighboring OH groups of CMC was thought to be responsible for this behavior, leading to an increase in the density of the films, and thus the films became more packed. The establishment of chemical bonds between the CMC chains and CuO-NPs and the emergence of certain localized states between the HOMO and LUMO bands of CMC, which result in a feasible smaller energy transition, can be linked to the reduction in the energy gap. Additionally, it may be connected to the rise in CMC's disorder level with rising CuO-NPs levels. Additionally, these findings agree well with the XRD analysis of the prepared films. Strong scientific interest exists in the relationships between the bandgap (E Opt ) and refractive index (n). The material's transparency and response to electromagnetic waves were indicated by the refractive index. Due to its critical function in optical fiber technology, planer waveguides, and optoelectronics, its determination is crucial.
The extinction coefficient (k) is among the most important optical properties that affect the material absorption when radiation is absorbed. The extinction coefficient (k) was calculated using the following equation 7 : As demonstrated in Fig. 8b, the extinction coefficient of CMC/CuO nanocomposite and pure CMC fluctuates with photon wavelength. As the concentration of CuO-NPs increased, the extinction coefficient of the CMC film increased. This behavior of the extinction coefficient can be explained by an increase in the number of charge carriers as a consequence of the rising absorption coefficient. In addition, the interaction between the energy carried in the samples and the incident light causes polarization of the medium charges, resulting in a loss of incident photon energy. This indicates that CuO-NPs will alter the structure of the CMC matrix.
Optical dispersion parameters. The Wemple-DiDomenico single oscillator (WDD) model was also used to investigate the refractive index dispersion in the non-absorbing zone (hv < Eg). It is critical to investigate the dispersion performance of such polymeric nanocomposite for optics and similar applications 58 . Thus, the prepared pristine CMC and CuO-NPs filled CMC nanocomposite films' oscillator (E o ) and dispersion (E d ) energies were calculated. The oscillator energy (E o ) represents the average bandgap of the material, whereas the dispersion energy (E d ) refers to the average strength of the interband transition, which is given by where E o and E d , stand for the single oscillator and dispersion energies, respectively. It is important to note that the WDD model is applicable in the region where the incident photons' energy (hv) is less than the optical bandgap and dependent on the refractive index (n) of these nanocomposite films. The single term "Sellmeier oscillator relations" could be used to derive a number of new optical constants at this area where the absorption vanishes (i.e., at an infinite wavelength) 58-60 :  www.nature.com/scientificreports/ where, ε l stands for the lattice dielectric constant, ε ∞ for the infinite dielectric constant, e for the electronic charge, C for the speed of light, ε o for the dielectric constant of free space, N for the concentration of free carriers, and m* for the effective mass. E o and E d of the pure and filled CMC films were determined from the plots of 1/(n 2 -1) as a function of (hv) 2 , as shown in Fig. 8c, in accordance with Eq. (14). The slope is equal to -1/(E o E d ), while the intercepts with the vertical axis of the linear sections equal to (E o /E d ). Table 7 contains the obtained E o and E d values. It should be noted that the CMC film's E o value is 5.00 eV, which is higher than that of any filled nanocomposite film. Additionally, E o falls to 2.86 eV as the nanofillers' content increases to 8 wt.%, while the E d value increased when the concentration of the nanofillers increased to 8 wt.%. Since E o is related to the optical energy bandgap and behaves similarly to it as explained above using Tauc's equation, these results are understandable. In other words, as filling introduces localized states and defects into the nanocomposite films as opposed to the pristine CMC, E o drops as the concentration of nanofillers increases, just as E g does. The rise in the degree of disordering and subsequent reinforcing of the optical transitions is what is responsible for the nanocomposite films' increased E d values as compared to pristine ones 60 .
The standard Sellmeier oscillator model (Eqs. 15, 16, and 17) is used to calculate additional optical parameters, such as the infinite dielectric constant ( ε ∞ ), lattice dielectric constant ( ε l ), the ratio of free carrier concentration to effective mass (N/m*), and the free carrier concentration (N) for the produced films in the non-absorption area in addition to the dispersion parameters determined above. According to Fig. 8d, the infinite dielectric constant was calculated by linearly fitting 1/(n 2 -1) plots against λ -2 for the unfilled and filled CMC films. The graph shows that the intercept of the fitted lines is related to ε ∞ by, ε ∞ = 1 intercept + 1 61 . Additionally, as illustrated in Fig. 8e, plotting is used to determine the ε l values represented by the intercepts of the extensions of the fitted linear lines in these plots, whereas N/m* values were calculated from the slops of these fitted lines. Table 7 contains a list of all the obtained optical constants ( ε ∞ , ε l , N/m*, and N). It is obvious that the optical properties of the manufactured nanocomposite films are directly influenced by the concentration of the nanofillers. Additionally, it was determined that the filling method significantly improves the infinite dielectric constant, lattice dielectric constant, the ratio of free carrier concentration to effective mass, and the free carrier concentration. For example, for 8 wt.% of CuO filled CMC nanocomposite films as compared to the pure one, the ratio of free carrier concentration to the effective mass (N/m*) increased by 11%, and the lattice dielectric constant increased by nearly 50%.
Additionally, it was noticed that the lattice dielectric constant for all prepared nanocomposite films is greater than the infinite one. This conduct is a result of the free carriers' contribution as presented in Table 7. Table 8 presents all of the optical parameters determined for pure CMC and CMC filled with 2, 4, 6, and 8 wt. % of CuO-NPs, including the onset band gap and HOMO/LUMO band gap using the Tauc and ASF models, respectively, the Urbach energy, T% at 300 and 600 nm, oscillation and dispersion energies, infinite and lattice dielectric constants, and the free carrier concentration (N). According to Table 8, adding different weight percentages of CuO-NPs to the CMC matrix results in a decrease in optical bandgap energy (both onset and HOMO/LUMO gaps), an increase in Urbach energy, a decrease in transmittance percent, a decrease in oscillation energy, an increase in dispersion energy, infinite and lattice dielectric constants, and free carrier concentration. Decreasing the T% to (17)   www.nature.com/scientificreports/ 1.10% and 2.06% at 300 and 600 nm, respectively, confirms that CMC /CuO nanocomposite films can be used as broadband UV-visible filters. Thus, CuO-NPs filled CMC nanocomposite films are now qualified as viable options for several optical and storage applications based on our findings, such as blocking material for UV radiation.

Conclusion
By using the solution casting approach, CMC films loaded with different concentrations (0-8 wt.%) of CuO-NPs were created. The amorphous character of the pure CMC film and the formation of copper oxide NPs in the tenorite phase (CuO) are both visible in the XRD examination. The host matrix's amorphous feature has increased as a result of the loading with CuO-NPs. This increase is thought to be due to the increased disordering of CMC with CuO filling. FTIR results confirm the formation of hydrogen bonding between CMC and CuO-NPs, which reflects the formation of a nanocomposite. HRTEM images reveal that CuO nanopowder is formed as a result of (agglomerated) CuO aggregates, which are made up of clusters of considerably smaller CuO crystallites. The effect of CuO-NPs concentration on the optical properties of nanocomposite films has been investigated using UV-Vis-NIR spectra measurements. UV-Vis-NIR demonstrates that the optical transmittance of pure CMC film is greater than 80%, and it declines as CuO-NPs are added. The results showed that the addition of CuO-NPs reduced light transmission significantly in both the UV and visible light bands, thus CMC/ CuO nanocomposite films can be used a UV blocker. Due to the localized states produced, the loading of CuO-NPs reduces the optical bandgap of the host matrix. The addition of CuO-NPs improves the refractive index of the CMC. Using the WDD model, the dispersion parameters of the unfilled and filled CMC nanocomposite films have been examined. This outcome might be understood in terms of the increase in the dispersion and reflection processes compared to pristine CMC film. The dispersion energy, oscillation energy, infinity dielectric constant, lattice dielectric constant, and other parameters are all significantly impacted by the CuO-NPs loading. According to the data, CMC loaded CuO-NPs are recommended for use in various optical and storage applications.